CN114457297B - Method for reducing thermoplastic deformation resistance of injection-molded aluminum alloy - Google Patents
Method for reducing thermoplastic deformation resistance of injection-molded aluminum alloy Download PDFInfo
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- CN114457297B CN114457297B CN202210046255.6A CN202210046255A CN114457297B CN 114457297 B CN114457297 B CN 114457297B CN 202210046255 A CN202210046255 A CN 202210046255A CN 114457297 B CN114457297 B CN 114457297B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D23/00—Casting processes not provided for in groups B22D1/00 - B22D21/00
- B22D23/003—Moulding by spraying metal on a surface
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/115—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by spraying molten metal, i.e. spray sintering, spray casting
Abstract
A method for reducing the thermoplastic deformation resistance of an aluminum alloy formed by injection belongs to the technical field of aluminum alloy processing. Carrying out high-temperature short-time heat preservation on the aluminum alloy sample subjected to densification spray forming before deformation; then carrying out thermoplastic deformation; the high-temperature heat preservation temperature is 420 ℃, the heat preservation time is 0-4 h and is not 0; and (5) water quenching after heat preservation. The microstructure of the alloy can be effectively controlled, and the hot working performance is improved. The method utilizes the alloy deformation resistance and the dynamic recrystallization behavior in the aluminum alloy reheating deformation process to establish a hot processing system, has wide applicability, is easy to realize industrial scale production, and is suitable for various aluminum alloy materials. The operation is simple, the consideration is comprehensive, and the practicability is strong.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy processing, and particularly relates to a method for reducing the thermoplastic deformation resistance of an aluminum alloy.
Background
The aluminum alloy has the advantages of small density, small specific strength and rigidity, corrosion resistance, easy forming and the like, and is widely applied to the fields of aerospace, shipbuilding and automobiles. The Al-Zn-Mg-Cu has the advantage of high corrosion resistance, is widely applied to fuselage frames, wing structures and high-strength structural parts of airplanes, and has an indispensable effect in the field of aerospace. Compared with the traditional cast alloy, the alloy has higher density, better weldability and corrosion resistance by using the spray forming process as a forming method. The spray forming technology has higher solidification rate and high alloying degree, can effectively eliminate macro segregation, obtains fine and uniform microstructures, and has great advantages in preparing large-size and high-alloying ingot blanks. However, spray forming Al-Zn-Mg-Cu aluminum alloy ingots has a number of drawbacks, and therefore the alloys are densified. After densification, a large amount of precipitated phases exist in the alloy and are distributed along the extrusion direction, which can affect further hot working deformation, affect the deformation resistance and recrystallization of the alloy and finally affect the performance of the aluminum alloy. In addition, the alloy has large forward extrusion ratio and deformation resistance, is difficult to form, and the material undergoes large deformation and dynamic recrystallization simultaneously, and the local dynamic recrystallization structure is easy to generate coarse crystal defects during solution treatment due to the nonuniformity of plastic deformation, thereby causing uneven structure performance. Rong Li et al (CN 113234974A) regulates alloy pre-precipitation to pre-precipitate a second phase, thereby reducing the deformation resistance of the alloy. A large amount of micron-sized particles are precipitated from the spray-formed alloy, and the precipitated phase is redissolved by heating in the hot working process, so that the influence of different hot working times on the precipitation condition of the alloy needs to be researched, the precipitated phase is further exerted, the solid solution strengthening effect of the alloy is reduced, and the deformation resistance of the alloy is reduced.
Disclosure of Invention
In order to overcome the defects, the invention provides a method for reducing the deformation resistance of the injection-molded aluminum alloy, which fully considers the influence of the deformation heat-preservation time on a precipitation phase and a deformation mechanism. The method combines rheological behavior and dynamic recrystallization, so that the aluminum alloy is thermally deformed after heat preservation in a short time, the plastic forming capability of the spray-formed aluminum alloy is further improved, and the thermal deformation aluminum alloy with uniform and fine structure and excellent comprehensive mechanical properties is obtained.
In order to achieve the purpose, the invention adopts the following technical scheme:
a method of reducing the deformation resistance of an aluminum alloy comprising the steps of:
(1) Carrying out high-temperature short-time heat preservation on the aluminum alloy sample subjected to densification spray forming before deformation;
(2) Then thermoplastic deformation is carried out.
Wherein the step (1) is sampling from a spray-formed aluminum alloy ingot, the aluminum alloy sample is Al-Zn-Mg-Cu alloy, and the alloy is Al- (7.6-8.4) Zn- (1.8-2.3) Mg- (2.0-2.6) Cu aluminum alloy.
The high-temperature heat preservation temperature in the step (1) is 420 ℃, the heat preservation time is 0-4 h and is not 0. And (5) water quenching after heat preservation.
And (3) the thermoplastic deformation in the step (2) is thermal compression, and the strain rate and the strain quantity are selected to obtain thermoplastic deformation data. Samples were run at 10 ℃/s -1 The temperature is raised to 420 ℃, and the isothermal hot compression experiment is carried out according to the test scheme after the temperature is kept for 1 min. According to the selected thermal deformation parameter range, a test scheme is designed, the deformation temperature is 420 ℃, and the strain rate is 0.01,0.1,1 and 10s -1 The strain is 0.6, and the steel plate is put into water for quenching after thermal deformation; and drawing a true stress-true strain curve according to the thermal simulation experiment data to obtain the alloy deformation resistance.
The invention has the advantages of
(1) The invention fully considers the influence of the deformation heating and heat preservation time on the precipitation phase and the thermal change behavior of the alloy, and ensures that the alloy has lower plastic deformation resistance and stable deformation mechanism.
(2) The invention can obtain the aluminum alloy processing product with good processing performance, has high processing efficiency and strong practicability and is easy to popularize.
Drawings
FIG. 1 is a back-scattered electron image of different times of heating and incubation. Heating for 420 deg.C/0 h, (b) heating for 420 deg.C/2 h, and (c) heating for 420 deg.C/4 h.
FIG. 2 is a graph of true stress versus true strain for various strain rates, where (a) is 10s -1 (b) is 1s -1 (c) is 0.1s -1 (d) is 0.01s -1 。
FIG. 3 is a schematic diagram of EBSD of example 1, wherein (a) is a graph showing the variation of percent recrystallization and (b) is a variation of grain orientation.
The specific implementation mode is as follows:
the present invention will be further described with reference to specific examples, but the present invention is not limited to the following examples.
1. The Al-Zn- (8.40) Mg- (2.00) Cu- (2.36) aluminum alloy is spray-formed as an example. Taking materials from the densification pressing plate, and turning the materials into a cylindrical small sample required by a thermal simulation experiment, wherein the size of the sample is phi 8 multiplied by 12mm. Heating the sample at 420 ℃ for 0h, 2h and 4h, then water quenching, and immediately carrying out thermal simulation experiment on the cylindrical sample by using a Gleeble-3500 thermal simulation testing machine. The deformation temperature is 420 ℃, and the strain rate is selected to be 0.01-10s -1 . Samples were run at 10 ℃/s -1 The temperature is raised to 420 ℃, the isothermal hot compression experiment is carried out according to the test scheme after the temperature is kept for 1min, the compression is stopped when the deformation reaches 60 percent, and the sample is quickly put into water for quenching.
2. The precipitated phase appeared to be redissolved after the sample was heated and incubated, as shown in FIG. 1.
3. According to the data obtained by the thermal simulation experiment, the true stress-true strain curve of the alloy under different deformation conditions is drawn, and is shown in figure 2.
Example 1
Analysis of the alloy flow stress curve of FIG. 2, table 1 below shows a strain rate of 10S -1 Peak stress and percent peak stress reduction, the results show: at a strain rate of 10S -1 When the alloy is deformed, the heating time before the deformation of the alloy is reduced, so that the deformation resistance of the alloy can be reduced, and the reduction percentage can reach 7.6 percent.
TABLE 1 Strain Rate of 10S -1 Peak stress and percent peak stress reduction of
Example 2
Analysis of the alloy flow stress curve of FIG. 2, table 2 below shows the strain rate of 1S -1 And percent reduction in peak stress, the results show that: at a strain rate of 1S -1 When the alloy is deformed, the heating time before the deformation of the alloy is reduced, so that the deformation resistance of the alloy can be reduced, and the reduction percentage can reach 20.68 percent.
TABLE 2 Strain Rate of 1S -1 Peak stress and percent peak stress reduction of
Example 3
Analysis of the alloy flow stress curve of FIG. 2, table 3 below shows a strain rate of 0.1S -1 Peak of (2)Value stress, the results show that: at a strain rate of 0.1S -1 When the alloy is deformed, the heating time before the deformation of the alloy is reduced, so that the deformation resistance of the alloy can be reduced, and the reduction percentage can reach 12.47 percent.
TABLE 3 Strain Rate of 0.1S -1 Peak stress and percent peak stress reduction of
And the strain rate is selected to be 0.1 ℃/s in the 'true stress-strain curve under different conditions of alloy' in figure 2 -1 Samples thermally deformed at different heat holding times were analyzed for Electron Back Scattering Diffraction (EBSD) (see figure 3). The heat preservation time is 2h, the recrystallization fraction is reduced to 41.78 percent, and the substructure increase accounts for 44.68 percent. The holding time was further increased to 4h, the recrystallization fraction was further decreased to 39.81% and the substructure was further increased to 46.00%. With the increase of the holding time before deformation, the alloy turns to large-angle crystal boundaries from the small-angle crystal boundaries more, the recrystallization fraction is reduced, and the substructure fraction is increased.
Example 3 demonstrates that the resistance to deformation of the alloy can be significantly reduced by reducing the holding time during the deformation process and increasing the recrystallization of the alloy.
Example 4
Analysis of the alloy flow stress curve of FIG. 2, table 4 below shows a strain rate of 0.01S -1 The results show that: at a strain rate of 0.01S -1 When the alloy is deformed, the heating time before the deformation of the alloy is reduced, so that the deformation resistance of the alloy can be reduced, and the reduction percentage can reach 10.01 percent.
TABLE 4 Strain Rate of 0.01S -1 Peak stress and percent peak stress reduction of
Therefore, the invention determines the proper hot working process parameters by considering the heating and heat preservation time of the hot working process and fully considers the recrystallization process of the alloy, thereby being beneficial to reducing the deformation resistance of the spray-formed aluminum alloy.
Claims (1)
1. A method of reducing the deformation resistance of an aluminum alloy, comprising the steps of:
(1) Carrying out high-temperature short-time heat preservation on the aluminum alloy sample subjected to densification spray forming before deformation;
(2) Then carrying out thermoplastic deformation;
sampling from an aluminum alloy cast ingot formed by injection, wherein an aluminum alloy sample is Al-Zn-Mg-Cu alloy, and the alloy is Al- (7.6-8.4) Zn- (1.8-2.3) Mg- (2.0-2.6) Cu aluminum alloy;
the high-temperature heat preservation temperature of the step (1) is 420 ℃, the heat preservation time is 0-4 h and is not 0; water quenching is carried out after heat preservation;
the step (2) of thermal deformation is thermal compression, strain rate and strain quantity are selected to obtain thermal deformation data, the deformation temperature range is 250-500 ℃, and the strain rate is 0.01-10s -1 The strain is 0.6, and the steel plate is put into water for quenching after thermal deformation;
the thermoplastic deformation is: samples were run at 10 ℃/s -1 The temperature is raised to 420 ℃, the isothermal hot compression experiment is carried out according to the test scheme after the temperature is kept for 1min, the compression is stopped when the deformation reaches 60 percent, and the sample is quickly put into water for quenching.
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| WO2008105303A1 (en) * | 2007-02-28 | 2008-09-04 | Kabushiki Kaisha Kobe Seiko Sho | High-strength and high-ductility al alloy and process for production of the same |
| CN106216680B (en) * | 2016-09-14 | 2018-08-24 | 中南大学 | A kind of hot-working of the aluminum silicon alloy plate of powder sintered preparation and heat treatment process |
| CN109735750A (en) * | 2019-01-08 | 2019-05-10 | 北京工业大学 | A kind of the Al-Zn-Mg-Cu-Er-Zr alloy and its preparation process of high strength anti-corrosion |
| CN111487129A (en) * | 2020-04-16 | 2020-08-04 | 江苏豪然喷射成形合金有限公司 | Method for testing room-temperature tensile mechanical properties of 7055 ultra-high-strength aluminum alloy extruded material formed by spraying |
| CN113234974B (en) * | 2021-05-07 | 2022-07-01 | 北京工业大学 | Method for reducing thermoplastic deformation resistance of Er microalloyed 7000 series aluminum alloy |
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